WO2014070356A1 - Nickel-based superalloy and articles - Google Patents

Nickel-based superalloy and articles Download PDF

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Publication number
WO2014070356A1
WO2014070356A1 PCT/US2013/062980 US2013062980W WO2014070356A1 WO 2014070356 A1 WO2014070356 A1 WO 2014070356A1 US 2013062980 W US2013062980 W US 2013062980W WO 2014070356 A1 WO2014070356 A1 WO 2014070356A1
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WIPO (PCT)
Prior art keywords
composition
matter
amounts
exemplary embodiments
rhenium
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PCT/US2013/062980
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English (en)
French (fr)
Inventor
Wei-Jen ZHANG
Douglas Gerard Konitzer
Joshua Leigh Miller
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General Electric Company
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Filing date
Publication date
Application filed by General Electric Company filed Critical General Electric Company
Priority to BR112015009718A priority Critical patent/BR112015009718B8/pt
Priority to CN201380057343.5A priority patent/CN104736731B/zh
Priority to JP2015539614A priority patent/JP6248117B2/ja
Priority to EP13774916.4A priority patent/EP2914757B1/en
Priority to CA2889343A priority patent/CA2889343C/en
Publication of WO2014070356A1 publication Critical patent/WO2014070356A1/en

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
    • C—CHEMISTRY; METALLURGY
    • C30—CRYSTAL GROWTH
    • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
    • C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
    • C—CHEMISTRY; METALLURGY
    • C30—CRYSTAL GROWTH
    • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
    • C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
    • C30B29/10—Inorganic compounds or compositions
    • C30B29/52—Alloys
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
    • F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
    • F01D5/12—Blades
    • F01D5/28—Selecting particular materials; Particular measures relating thereto; Measures against erosion or corrosion
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/04—Heavy metals
    • F05C2201/0433—Iron group; Ferrous alloys, e.g. steel
    • F05C2201/0466—Nickel

Definitions

  • This invention relates generally to compositions of matter suitable for use in aggressive, high-temperature gas turbine environments, and articles made therefrom.
  • Nickel-based single crystal superalloys are used extensively throughout the aeroengine in turbine blade, nozzle, and shroud applications. Aeroengine designs for improved engine performance demand alloys with increasingly higher temperature capability, primarily irs the form of improved creep strength (creep resistance). Alloys with increased amounts of solid solution strengthening elements such as Ta, W, Re, and Mo, which also provide improved creep resistance, generally exhibit decreased phase stability, increased density, and lower environmental resistance. Recently, thermal-mechanical fatigue (TMF) resistance has been a limiting design criterion for turbine components. Temperature gradients create cyclic thermally induced strains that promote damage by a complex combination of creep, fatigue, and oxidation. Directionally solidified superalloys have not historically been developed for cyclic damage resistance. However, increased cyclic damage resistance is desired for improved engine efficiency.
  • TMF thermal-mechanical fatigue
  • Single crystal superalloys may be classified into four generations based on similarities in alloy compositions and high temperature mechanical properties. So-called first generation single crystal superalloys contain no rhenium. Second generation superalloys typically contain about three weight percent rhenium. Third generation superalloys are designed to increase the temperature capability and creep resistance by raising the refractory metal content and lowering the chromium level. Exemplary alloys have rhenium levels of about 5.5 weight percent and chromium levels in the 2-4 weight percent range. Fourth and fifth generation alloys include increased levels of rhenium and other refractory metals, such as ruthenium.
  • Second generation alloys are not exceptionally strong, although they have relatively stable microstructures.
  • Third and fourth generation alloys have improved strength due to the addition of high levels of refractory metals.
  • these alloys include high levels of tungsten, rhenium, and ruthenium. These refractory metals have densities that are much higher than that of the nickel base, so their addition increases the overall alloy density.
  • fourth generation alloys may be about 6% heavier than second generation alloys. The increased weight and cost of these alloys limit their use to only specialized applications.
  • Third and fourth generation alloys are also limited by microstractural instabilities, which can impact long-term mechanica! properties.
  • third generation superai!oys provide a 50°F (about 28 ° C) improvement in creep capability relative to second generation s peralloys.
  • Fourth and fifth generation superalloys offer a further improvement in creep strength achieved by high levels of solid solution strengthening elements such as rhenium, tungsten, tantalum, molybdenum and the addition of ruthenium,
  • Cyclic damage resistance is quantified by hold time or sustained-peak low cycle fatigue (SPLCF) testing, which is an important property requirement for single crystal turbine blade alloys.
  • SPLCF sustained-peak low cycle fatigue
  • the third and fourth generation single crystal superalloys have the disadvantages of high density, high cost due to the presence of rhenium and ruthenium, microstructural instability under coated condition (SRZ formation), and inadequate SPLCF lives.
  • Fatigue resistant nickel-based single crystal superalloys for turbine blade applications thai provide lower density, low rhenium and ruthenium content, low cost, improved SPLCF resistance, and less SRZ formation comparai to known alloys as well as balanced creep and oxidation resistance are described in various exemplary embodiments.
  • a composition of matter comprises from about 5 to about 7 wt% aluminum, from about 4 to about 8 wt% tantalum, from about 3 to about 8 wt% chromium, from about 3 to about 7 wt% tungsten, from 1 to about 5 wt% molybdenum, from 1.5 to about 5 wt% rhenium, from 5 to about 14 wt% cobalt, from about 0 to about 1 wt% hafnium, from about 0.01 to about 0.03 wt% carbon, from about 0.002 to about 0.006 wt% boron, and balance nickel and incidental impurities.
  • the composition may exhibit a sustained peak low cycle fatigue life at 1800°F/45 ksi of at least about 4000 cycles.
  • Exemplary embodiments disclosed herein include an article, such as a blade, nozzle, a shroud, a splash plate, and a combustor of a gas turbine engine, comprising a substantially single crystal having a composition comprising from about 5 to about 7 wt% aluminum, from about 4 to about 8 wt% tantalum, from about 3 to about 8 wt% chromium, from about 3 to about 7 wt% tungsten, from 1 to about 5 wt% molybdenum, from 1.5 to about 5 wt% rhenium, from 5 to about 14 wt% cobalt, from about 0 to about 1 wt% hafnium, from about 0,01 to about 0.03 wt% carbon, from about 0.002 to about 0.006 wt% boron, and balance nickel and incidental impurities.
  • the composition may exhibit a sustained peak low cycle fatigue life at 1800°F/45 ksi of at least about 4000 cycles
  • FIG. 1 is a perspective view of an article, such as a gas turbine blade, according to an embodiment of the invention.
  • FIG. 2 is a table setting forth exemplary compositions according to the invention and reference compositions.
  • FIG. 3 is a graph showing sustained peak low cycle fatigue life (SPLCF) (cycles) at 1800°F/45 ksi as a function of total Re and Ru concentration (wt%) for exemplary compositions according to the invention and reference compositions.
  • SPLCF sustained peak low cycle fatigue life
  • FIG. 4 is a graph showing rupture tolerance (hours) at 2000°F/20 ksi as a function of total Re and Ru concentration (wt%) for exemplary compositions according to the invention and reference compositions.
  • FIG. 5 is a block-flow diagram illustrating an approach for preparing an article according to the invention.
  • This invention describes the chemistries of Ni-based single crystal superalloys for turbine blade applications.
  • the superalloys provide lower density, low rhenium and ruthenium content, low cost, improved SPLCF resistance, and less SRZ formation compared to known alloys, as well as balanced creep and oxidation resistance.
  • the improvement of fatigue resistance was achieved by balancing the strength, oxidation and creep resistance of the alloys through controlling the amount of gamma strengtheners such as W, Mo, Re, Co and Cr and by controlling the volume fraction of gamma prime phase by controlling the concentration of Al, Ta, Hf.
  • the invention is described in various exemplary embodiments.
  • FIG. 1 depicts a component of a gas turbine engine, illustrated as a gas turbine blade 10.
  • the gas turbine blade 10 includes an airfoil 12, a laterally extending platform 16, an attachment 14 in the form of a dovetail to attach the gas turbine blade 10 to a turbine disk (not shown), in some components, a number of cooling channels extend through the interior of the airfoil 12, ending in openings 18 in the surface of the airfoil 12.
  • the component article 10 is substantially a single crystal. That is, the component article 10 is at least about 80 percent by volume, and more preferably at least about 95 percent by volume, a single grain with a single crystallographic orientation. There may be minor volume fractions of other crystallographic orientations and also regions separated by low-angle boundaries.
  • the single-crystal structure is prepared by the directional solidification of an alloy composition, usually from a seed or other structure that induces the growth of the single crystal and single grain orientation.
  • exemplary alloy compositions discussed herein is not limited to the gas turbine blade 10, and it may be employed in other articles such as gas turbine nozzles, vanes, shrouds, or other components for gas turbine engines.
  • Exemplary embodiments disclosed herein may include aluminum to provide improved SPLCF resistance and oxidation resistance. Exemplary embodiments may include from about 5 to about 7 wt% aluminum. Other exemplary embodiments may include from about 5.5 to about 6.5 wt% aluminum. Other exemplary embodiments may include from about 5.5 to about 6.2 wt% aluminum. Other exemplary embodiments may include from about 6.1 to about 6.5 wt% aluminum. Other exemplary embodiments may include from about 6.2 to about 6.4 wt% aluminum.
  • Exemplary embodiments disclosed herein may include tantalum to promote gamma prime strength. Exemplary embodiments may include from about 4 to about 8 wt% tantalum. Other exemplary embodiments may include from about 4.5 to about 8 wt% tantalum. Other exemplar ⁇ ' embodiments may include from about 6 to about 8 wt% tantalum. Other exemplary embodiments may include from about 4 to about 6 wt% tantalum.
  • Exemplary embodiments disclosed herein may include chromium to improve hot corrosion resistance. Exemplary embodiments may include from about 3 to about 8 wt% chromium. Other exemplary embodiments may include from about 4 to about 6.5 wt% chromium. Other exemplary embodiments may include from about 4.3 to about 6.5 wt% chromium. Other exemplary embodiments disclosed herein may include from about 4.5 to about
  • 5 wt% chromium may include from about 5 to about 6.5 wt% chromium.
  • Other exemplary embodiments disclosed herein may include from about 5.5 to about
  • Exemplary embodiments disclosed herein may include tungsten as a strengthener. Exemplary embodiments may include from about 3 to about 7 wt% tungsten. Other exemplary embodiments may include tungsten in amounts from about 3 to about 6 wt%. Other exemplary embodiments may include tungsten in amounts from about 4 to about 6 wt%. Other exemplary embodiments may include tungsten in amounts from about 3.5 to about 6.5 wt%. Other exemplary embodiments may include tungsten in amounts from about 3.5 to about 6 wt%.
  • Exemplary embodiments disclosed herein may include molybdenum to impart solid solution strengthening. Exemplary embodiments may include from about 1 to about 5 wt% molybdenum. Other exemplary embodiments may include molybdenum in amounts from about 2 to about 5 wt%. Other exemplary embodiments may include molybdenum in amounts from about 2 to about 4 wt%. Other exemplary embodiments may include molybdenum in amounts from about 2 to about 3 wt%. Other exemplary embodiments may include molybdenum in amounts from about 1.5 to about 4 wt%. Other exemplary embodiments may include molybdenum in amounts from about 1 ,5 to about 2.5 wt%.
  • Exemplary embodiments disclosed herein may include rhenium, which is a potent solid solution strengthener that partitions to the gamma phase, and also is a slow diffusing element, which limits coarsening of the gamma prime. Exemplary embodiments may include from about 1.5 to about 5 wt% rhenium. Other exemplary embodiments may include rhenium at levels between about 2.5 to about 4,5 wt%. Other exemplary embodiments may include rhenium at levels between about 3 to about 4.2 wt%. Other exemplary embodiments may include rhenium at levels between about 3 to about 4 wt%. Other exemplary embodiments may include rhenium at levels between about 2.5 to about 4.5 wt%. Other exemplary embodiments may include rhenium at levels between about 3.5 to about 4.2 wt%.
  • Exemplary embodiments disclosed herein may include cobalt. Exemplary embodiments may include from about 5 to about 14 wt% cobalt. Other exemplary embodiments may include from about 7 to about 12.5 wt% cobalt. Other exemplar ⁇ ' embodiments may include from about 9 to about 12 wt% cobalt. Other exemplary embodiments may include from about 5 to about 8 wt% cobalt. Other exemplary embodiments may include from about 6.5 to about 7.5 wt% cobalt.
  • Exemplary embodiments disclosed herein may optionally include hafnium, which improves the oxidation and hot corrosion resistance of coated alloys. Hafnium may improve the life of thermal barrier coatings. Exemplary embodiments may include from about 0 to about 1 wt% hafnium. Other exemplary embodiments may include from about 0.2 to about 0.6 wt% hafnium.
  • Exemplary embodiments disclosed herein may include carbon. Exemplary embodiments may include from about 0.01 to about 0.03 wt% carbon. Other exemplary embodiments may include from about 0.015 to about 0.025 wt% carbon. Other exemplar ⁇ ' embodiments may include from about 0.015 to about 0.025 wt% carbon.
  • Exemplary embodiments disclosed herein may include boron to provide tolerance for low angle boundaries. Exemplary embodiments may include from about 0.002 to about 0.006 wt% boron. Other exemplary embodiments may include from about 0.0025 to about 0.0055 wt% boron. Other exemplary embodiments may include from about 0.003 to about 0.005 wt% boron. Other exemplary embodiments may include from about 0.0035 to about 0.0045% boron.
  • a composition of matter comprises from about 5 to about 7 wt% aluminum, from about 4 to about 8 wt% tantalum, from about 3 to about 8 wt% chromium, from about 3 to about 7 wt% tungsten, from 1 to about 5 wt% molybdenum, from 1.5 to about 5 wt% rhenium, from 5 to about 14 wt% cobalt, from about 0 to about 1 wt% hafnium, from about 0.01 to about 0.03 wt% carbon, from about 0.002 to about 0.006 wt% boron, and balance nickel and incidental impurities.
  • a composition of matter comprises from about 5,5 to about 6.5 wt% aluminum, from about 4.5 to about 8 wt% tantalum, from about 4 to about 6.5 wt% chromium, from about 3 to about 6 wt% tungsten, from 2 to about 5 wt% molybdenum, from 2.5 to about 4.5 wt% rhenium, from 7 to about 12,5 wt% cobalt, from about 0.2 to about 0.6 wt% hafnium, from about 0.015 to about 0.025 wt% carbon, from about 0.0025 to about 0.0055 wt% boron, and balance nickel and incidental impurities.
  • a composition of matter comprises from about 5.5 to about 6,5 wt% aluminum, from about 6 to about 8 wt% tantalum, from about 4.3 to about 6.5 wt% chromium, from about 4 to about 6 wt% tungsten, from 2 to about 4 wt% molybdenum, from 3 to about 4.2 wt% rhenium, from 7 to about 12.5 wt% cobalt, from about 0.2 to about 0,6 wt% hafnium, from about 0.015 to about 0.025 wt% carbon, from about 0.003 to about 0.005 wt% boron, and balance nickel and incidental impurities.
  • a composition of matter comprises from about 5.5 to about 6.2 wt% aluminum, from about 6 to about 8 wt% tantalum, from about 4.5 to about 5 wt% chromium, from about 4 to about 6 wt% tungsten, from 2 to about 3 wt% molybdenum, from 3 to about 4 wt% rhenium, from 9 to about 12.0 wt% cobalt, from about 0.2 to about 0.6 wt% hafnium, from about 0.015 to about 0.025 wt% carbon, from about 0.0035 to about 0.0045 wt% boron, and balance nickel and incidental impurities.
  • a composition of matter comprises from about 6.1 to about 6.5 wt% aluminum, from about 4 to about 6 wt% tantalum, from about 5 to about 6.5 wt% chromium, from about 3.5 to about 6,5 wt% tungsten, from 1.5 to about 4 wt% molybdenum, from 2.5 to about 4,5 wt% rhenium, from 5 to about 8 wt% cobalt, from about 0.2 to about 0.6 wt% hafnium, from about 0.015 to about 0.025 wt% carbon, from about 0.003 to about 0.005 wt% boron, and balance nickel and incidental impurities.
  • a composition of matter comprises from about 6.2 to about 6.4 wt% aluminum, from about 4 to about 6 wt% tantalum, from about 5.5 to about 6 wt% chromium, from about 3.5 to about 6 wt% tungsten, from 1.5 to about 2.5 wt% molybdenum, from 3.5 to about 4.2 wt% rhenium, from 6.5 to about 7.5 wt% cobalt, from about 0.2 to about 0.6 wt% hafnium, from about 0.015 to about 0.025 wt% carbon, from about 0.0035 to about 0.0045 wt% boron, and balance nickel and incidental impurities.
  • Exemplary embodiments disclosed herein include an article, such as a blade, nozzle, a shroud, a splash plate, and a combustor of a gas turbine engine, comprising a substantially single crystal having a composition comprising from about 5 to about 7 wt% aluminum, from about 4 to about 8 wt% tantalum, from about 3 to about 8 wt% chromium, from about 3 to about 7 wt% tungsten, from 1 to about 5 wt% molybdenum, from 1.5 to about 5 wt% rhenium, from 5 to about 14 wt% cobalt, from about 0 to about 1 wt% hafnium, from about 0.01 to about 0.03 wt% carbon, from about 0.002 to about 0.006 wt% boron, and balance nickel and incidental impurities.
  • FIG. 2 Exemplary compositions according to the invention and reference compositions are presented in the FIG. 2.
  • alloys A1-A6 have compositions according to the invention.
  • Reference alloys R1-R.5 have compositions that fall outside of the compositional ranges according to the invention, as described above.
  • FIG, 2 also provides the sustained-peak low cycle fatigue resistance (SPLCF) (cycles) at 1800°F/45 ksi and rupture life at 2000°F/20 ksi (hours) for alloys A1-A6 as well as reference alloys R1-R5.
  • SPLCF sustained-peak low cycle fatigue resistance
  • the alloys Al, A5, and A6 have SPLCF and rapture tolerances greater than reference alloys R1 -R5.
  • the alloys according to an embodiment of the invention exhibit a SPLCF greater than about 4000 cycles at 1800°F/45 ksi and a rupture of greater than about 150 hours at 200G°F/20 ksi.
  • alloy Al has a SPLCF of about 41 1 1 cycles and a rupture life of about 155 hours.
  • the alloys according to another embodiment of the invention generally exhibit a SPLCF greater than about 5000 cycles at 1800°F/45 ksi and a rupture life of greater than about 200 hours at 2000°F/20 ksi.
  • A5 has a SPLCF of about 5497 cycles and a rupture life of about 203 hours
  • alloy A6 has a SPLCF of about 5219 cycles and a rapture life of about 211 hours.
  • FIG. 3 is a graph showing SPLCF life (cycles) at 1800°F/45 ksi as a function of total Re and Ru concentration (wt%) for exemplary compositions according to the invention and reference compositions.
  • FIG. 4 is a graph showing rupture life (hours) at 2000°F/20 ksi as a function of total Re and Ru concentration (wt%) for exemplary compositions according to the invention and reference compositions.
  • alloys Al, A5, and A6 according to the invention have much higher SPLCF and rupture lives than the reference alloys R1-R5 with similar or higlier Re + Ru concentrations.
  • alloys Al and A5 have a Re + Ru concentration of about 4 wt%
  • alloy A6 has a Re + Ru concentration of about 3.5 wt%.
  • Reference alloys R3- R5 have higlier Re + Ru concentrations than alloys Al , A5, and A6, but exhibit lower SPLCF and rupture lives than alloys Al , A5, and A6.
  • FIG. 5 is a block-flow diagram illustrating an approach for preparing an article according to the invention.
  • An alloy having the composition set forth above is prepared, as shown at reference numeral 20.
  • the alloy is melted and solidified as substantially a single crystal, as shown at reference numeral 22.
  • Techniques for solidifying single crystal articles are well-known in the art. Generally, they involve solidifying the alloy in a mold unidirectionalSy from one end of the article, with a seed or growth constriction defining the single crystal orientation that is desired in the article.
  • the article is prepared with a [001] crystallographic direction parallel to a long axis of the article in the case of the turbine blade or turbine vane.
  • Post processing may include, but is not limited to heat treating the article to optimize the mechanical properties of the alloy and/or machining the article.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Inorganic Chemistry (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Crystals, And After-Treatments Of Crystals (AREA)
PCT/US2013/062980 2012-10-31 2013-10-02 Nickel-based superalloy and articles WO2014070356A1 (en)

Priority Applications (5)

Application Number Priority Date Filing Date Title
BR112015009718A BR112015009718B8 (pt) 2012-10-31 2013-10-02 composição de superliga de cristal único à base de níquel e artigo.
CN201380057343.5A CN104736731B (zh) 2012-10-31 2013-10-02 镍基超合金和制品
JP2015539614A JP6248117B2 (ja) 2012-10-31 2013-10-02 ニッケル基超合金および物品
EP13774916.4A EP2914757B1 (en) 2012-10-31 2013-10-02 Nickel-based superalloy and articles
CA2889343A CA2889343C (en) 2012-10-31 2013-10-02 Nickel-based superalloy and articles

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US13/665,280 2012-10-31
US13/665,280 US8858876B2 (en) 2012-10-31 2012-10-31 Nickel-based superalloy and articles

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EP (1) EP2914757B1 (enrdf_load_stackoverflow)
JP (1) JP6248117B2 (enrdf_load_stackoverflow)
CN (1) CN104736731B (enrdf_load_stackoverflow)
BR (1) BR112015009718B8 (enrdf_load_stackoverflow)
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WO2016156806A1 (en) * 2015-04-01 2016-10-06 Oxford University Innovation Limited A nickel-based alloy
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